Pressure casting method of magnesium alloy and metal products thereof

ABSTRACT

The present invention provides a pressure casting method of a magnesium alloy. In the method, a molten magnesium alloy is cooled to form a partially molten state containing a solid-phase, and the partially molten state is further cooled to form a solid-phase granularly crystallized solid material. The solid material is partially-melted and pressure cast into a mold by a molding machine. A ratio of primary crystals in said solid material is set to 55 to 65%. The solid material is partially-melted in a solid-phase and liquid-phase coexisting state at a selected heating temperature so that a semi-solid having a thixotropic properties and having the size of a main solid phase of 50 to 250 μm and a solid-phase ratio of 30 to 70% is formed. The semi-solid is pressure cast into a mold through a nozzle while maintaining the semi-solid state to form metal products having a ratio of primary crystals of 20 to 50%.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a casting method of using a granularly crystallized magnesium alloy solid as a casting materials, melting the solid material to a solid- phase and liquid-phase coexisting state to form metal products by a pressure casting means and relates to their metal products.

2. Description of the Related Art

In a conventional manufacturing method for a product from a partially molten metal, a molten alloy is held in a solid-phase and liquid-phase coexisting state in an insulating vessel for a desired time, generating many fine spherical primary crystals and pressure casting them in a mold of a die cast machine at a desired liquid phase ratio to form cast products (see for example Patent Reference 1).

Further, in molding of metal products using a magnesium alloy, a solid material potentially holding thixotropy is heated in a partially molten state and the obtained material is charged into a mold by an injection apparatus (see for example Patent Reference 2).

-   -   [Patent Reference 1]     -    Japanese A-HEI 9-10893 (on pages 3 to 5, FIG. 9)     -   [Patent Reference 2]     -    JP-A-2001-252759 (on pages 6 and 7, FIG. 1)

The above-mentioned patent reference 1 describes a pressure casting method of cast products by a die cast machine including the steps of pouring a molten alloy into a tilt cooling jig held at a temperature lower than the melting point to flow down and holding the alloy in an insulating vessel in a state at a temperature equal to or lower than a liquidus line temperature and higher than a eutectic temperature or a solidus line temperature for five seconds to 60 minutes to form the cast products in a liquid phase ratio of 20 to 90%, preferably 30 to 70%.

Further, the Patent Reference 2 describes a casting method including the steps of allowing a molten magnesium alloy to flow on a cooling tilt plate to cool in a partially molten, reserving the alloy in a reservoir until it becomes a metal slurry having fine spherical crystals, then solidifying the slurry by rapid cooling to form a metal material potentially holding a thixotropy performance, and melting the metal material into a partially molten state magnesium alloy exhibiting a thixotropy performance to charge into a mold by an injection apparatus.

In the prior art described in Patent Reference 1, after a molten alloy is cooled in a partially molten state the obtained alloy must be held in an insulating vessel until it has a desired liquid phase ratio. Thus it takes much time from the melting of the material to pressure casting of products. In order to shorten the time, many insulating vessels and their transfer means are required. Further, since the material is cooled close to lower temperature close to the casting temperature and is transferred to a molding machine to conduct molding immediately, some molding machines have a problem, which cannot be adopted.

Even in the prior art described in Patent Reference 2, since the solid phase ratio of a partially molten slurry is high, so much time is also needed until holding the thixotropy performance potentially. However, the molding steps of remelting a rapid cooling solidified metal material in a partially molten state by a molding machine and pressure casting the obtained material into a mold in a state having a thixotropic properties can be completed for short time. Further, the supply of the metal material into the molding machine is also easy and continuous casting is also possible, whereby the prior art has adaptability to the casting machine.

However, in Patent Reference 2, it is difficult to set temperature conditions and holding time for metal slurry crystals crystallized out at a solid-phase and liquid-phase coexisting temperature region to be uniform spherical crystals, and there is a problem in maintaining a solid-phase ratio, which is preferable in molding. The present inventors have studied these problems. As a result they have found that even if crystals do not become uniform spherical ones, if a primary crystal ratio in which a solid material is granularly crystallized is within a certain range, the primary crystal becomes a sphered solid phase in a solid-phase and a liquid-phase coexisting state, and at the same time a main solid phase has a solid-phase ratio preferable for casting in a grain size of 50 μm or more, and that if the holding time is within 30 minutes, the material is pressure cast into molds without changing set conditions so that a number of metal products of a magnesium alloy extremely excellent in a distribution state of primary crystals can be formed.

SUMMARY OF THE INVENTION

In view of the above problems, the object of the present invention is to provide a new pressure casting method of a magnesium alloy comprising steps of melting previously granularly crystallized solid material to form a partially molten state (hereinafter referred to as a “semi-solid”) having a thixotropic properties in a solid-phase and liquid-phase coexisting state (hereinafter referred to as a “semi-solid”) and pressure casting the semi-solid into a mold, wherein the grain diameter and solid-phase ratio in a solid phase in the semi-solid are set to a preferable state for molding so that metal products having an excellent metal structure can be formed stably.

This invention comprises the steps of cooling a molten magnesium alloy to form a partially molten state containing a solid-phase, further cooling the partially molten state to form a solid-phase granularly crystallized solid material and partially-melting the solid material to pressure cast it into a mold by a molding machine, wherein a ratio of primary crystals of said solid material is set to 55 to 65%, the solid material is melted to be a semi-solid body in a solid-phase and liquid-phase coexisting state so that the semi-solid having a main solid phase of 50 to 250 μm and a solid-phase ratio of 30 to 70%, and pressure casting the semi-solid into a mold through a nozzle while maintaining the semi-solid state to form metal products having a ratio of primary crystals of 20 to 50%.

Further, in this invention, the temperature of a heating means in a casting machine for holding the semi-solid in the semi-solid state is set at a temperature 5 to 15° C. higher than the temperature of the semi-solid in accordance with the time from the starting of melting of the solid material to the pressure casting of the semi-solid. In addition, the semi-solid is pressure cast from a nozzle having a diameter of 8 to 15 mm into a mold through a gate having a thickness of 1 mm or less.

The metal product of this invention is a metal product molded by the above-mentioned pressure cast molding method of a magnesium alloy which comprises a metal structure whose main primary crystal is spherical and has a diameter of 10 μm or more, and has a wall thickness of 0.4 to 1.5 mm, preferably 0.6 to 1.0 mm.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1(A) is a view of a structure by a metallurgical micrograph of a magnesium alloy (AZ91D) used in a pressure casting molding method according to this invention, and FIG. 1(B) is a view in which the micrograph is two-valued in black and white by an image processing;

FIG. 2(A) is a view of a structure by a metallurgical micrograph of a solid obtained by rapidly cooling a semi-solid in a solid-phase and liquid-phase coexisting state (570° C.) and FIG. 2(B) is a view in which the micrograph is two-valued in black and white by an image processing;

FIG. 3(A) is a view of a structure by a metallurgical micrograph of a solid obtained by rapidly cooling the semi-solid after holding it for 30 minutes in a solid-phase and liquid-phase coexisting state (570° C.), and FIG. 3(B) is a view in which the micrograph was two-valued in black and white by an image processing;

FIG. 4(A) is a view of a structure by a metallurgical micrograph of a solid obtained by rapidly cooling a semi-solid in a solid-phase and liquid-phase coexisting state (590° C.) and FIG. 4(B) is a view which the micrograph is two-valued in black and white by an image processing;

FIG. 5(A) is a view of a structure by a metallurgical micrograph of a solid obtained by rapidly cooling the semi-solid after holding the semi-solid for 30 minutes in a solid-phase and liquid-phase coexisting state (590° C.), and FIG. 5(B) is a view in which the micrograph is two-valued in black and white by an image processing;

FIG. 6(A) is a view of a structure by a metallurgical micrograph of a metal product molded of a semi-solid in a solid-phase and liquid-phase coexisting state (580° C., holding time of 25 minutes), and FIG. 6(B) is a view in which the micrograph is two-valued in black and white by an image processing;

FIG. 7(A) is a view of a structure by a metallurgical micrograph of a metal product molded of a semi-solid in a solid-phase and liquid-phase coexisting state (585° C., holding time of 25 minutes), and FIG. 7(B) is a view in which the micrograph is two-valued in black and white by an image processing;

FIG. 8(A) is a view of a structure by a metallurgical micrograph of a metal product molded of a semi-solid in a solid-phase and liquid-phase coexisting state (590° C., holding time of 25 minutes), and FIG. 8(B) is a view in which the micrograph is two-valued in black and white by an image processing; and

FIG. 9(A) is a view of a structure by a metallurgical micrograph of a metal product molded of a semi-solid in a solid-phase and liquid-phase coexisting state (595° C., holding time of 25 minutes), and FIG. 9(B) is a view in which the micrograph is two-valued in black and white by an image processing.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

In each Figure, (A) is a photograph taken by a metallurgical microscope and (B) is a view in which a part of the photograph is two-valued into black and white by image processing and the grain diameter of a solid phase and the solid phase ratio or a primary crystal ratio are calculated from the dot number of the white and the black dots.

FIG. 1 shows a metal structure of a magnesium alloy (AZ91D) used as a solid material in this invention. The solid material of the granular crystal structure is manufactured by the steps of heating and melting a magnesium alloy at a temperature higher than the liquidus line temperature, allowing the molten alloy to flow down on a surface of a cooled (for example 60° C.) tilt plate, cooling the alloy to a temperature at which a solid-phase and liquid-phase below the liquidus line temperature coexist (hereinafter referred to as a solid-phase and liquid-phase coexisting temperature) to produce a solid phase, then holding the solid phase and liquid phase coexisting temperature for desired time until the solid phase ratio reaches 55 to 65% a primary crystal a of a solid material, and cooling the alloy below the solidus line temperature. As one example, the solid material is manufactured by cooling a magnesium molten alloy of 605° C. to a temperature 5° C. to 25° C. lower than 595° C. (the liquidus line temperature), holding the temperature in its range for one minute and then rapidly cooling the alloy below the solidus line temperature.

As the use form of the solid materials any type of the solid material such as a round bar, ingot or the like, and of a granular solid material such as a chip, pellet or the like may be selected. The material form can be optionally selected by a structure of the metal casting machine used. Further, as the metal casting machine, a metal casting machine having the same structure as an inline screw injection molding machine, a plunger injection molding machine, a (pre-plasticizing system) injection molding machine or the like, or a molding machine, which can pressure cast a semi-solid charged into a cylinder into a mold from a nozzle through a gate, such as a die cast machine or the like, may be all adopted.

The molding of metal products of the above-mentioned solid material is performed as follows. First, a solid material is made a semi-solid in a solid-phase and liquid-phase state at a selected melting temperature. Then the temperature of the semi-solid is held at the liquidus line temperature or less and the solidus line temperature or more to maintain a solid-phase and liquid-phase coexisting state. After that the semi-solid is pressure cast into a mold from a nozzle through a gate.

In the above-mentioned melting step, when a solid material reaches the solidus line temperature or more, eutectic crystals b in the metal structure are melted to be semi-solid liquid phases b′. And a primary crystal a is dispersed into the liquid-phase as a solid-phase a′. Alternatively, corners of the primary crystal a, which are liable to be influenced by heating, are melted to become sphered solid phases.

The size (grain diameter) of this main solid phase a′ and the solid-phase ratio of the semi-solid are changed in ranges of 50 to 250 μm and of 25 to 75%, respectively, by the melting temperature of the solid material and the holding temperature and time for the semi-solid. If the solid material has a solid phase a′ of a size in the range (most preferably 50 to 100 μm and, the average grain diameter of 80 μm) and a solid phase ratio of the range (preferably 30 to 70%), pressure casting into a mold can be carried out without any trouble while maintaining thixotropy performance (viscous fluid performance).

FIG. 2 is a metal structure of a solid obtained by rapid cooling a semi-solid produced when a solid material having a ratio of a primary crystal a of 61% and a grain diameter of 50 to 100 μm shown in FIG. 1 is melted at 570° C., without holding time. The primary crystal a of this solid material before melting has a solid phase a′ of 100 to 200 μm by melting so that the solid phase ratio is increased to 64%. Further, even a metal structure of a solid rapidly cooled after holding a semi-solid at a melting temperature of 570° C. for 30 minutes has no extreme enlargement of the solid phase a′ due to a lapse of time and grows generally, as shown in FIG. 3. However, the main solid phase a′ reaches a size of 150 to 250 μm and the solid phase ratio is increased to 69% at most.

FIG. 4 is a metal structure of a solid obtained by rapid cooling a semi-solid produced when a solid material is melted at 590° C., and the sizes of solid phases a′ are various, but in a range of 100 to 200 μm and the solid phase ratio is 48%. Further in a metal structure of a solid rapidly cooled after the semi-solid is held at a temperature of 590° C. for 30 minutes, as shown in FIG. 5, a solid-phase ratio is remarkably increased to 65%, but some sizes of solid phases a′ reach 50 to 250 μm in the grain diameter, which is smaller than before melting. This reason is guessed to be that since the holding temperature is close to the liquidus line temperature (595° C.), a small solid phase, which is liable to be thermally influenced, is partially melted so that the size of the diameter is decreased.

In the above-mentioned semi-solids at the temperatures of 570° C. and 590° C., the almost solid phases a′ are sphered and the size of the solid phase and solid-phase ratio are further increased as compared with a solid material. Further, the solid-phase ratios during melting are 48% at 590° C., and 64% at 570° C. That is when the temperature is high, melted parts are increased, resulting in a decreased solid-phase ratio. However, all solid-phase ratios of the solid materials held for 30 minutes do not exceed 70% and the sizes of the solid phases a′ are in a range of 50 to 200 μm. This means that if the semi-solid maintains a solid-phase and liquid-phase coexisting state, it can be pressure cast into a mold at the same set conditions in a state having thixotropy performance until at least 30 minutes have passed.

Further, a temperature of a heating means in a molding machine for maintaining the material at a semi-solid state can be set at about 5 to 15° C. higher than the temperature of a semi-solid in accordance with time from the starting of melting of the solid material to the pressure casting of the semi-solid. It is only that a solid phase and liquid phase coexisting state is maintained until the pressure casting whereby a state where the thixotropy performance is produced, exists.

In a semi-solid having a low solid phase ratio of 25% or less, even if the semi-solid is in a solid phase and liquid phase coexisting state, the liquid phase ratio is too much and the fluidity is increased. Thus, the semi-solid does not have appropriate thixotropy performance or a shortage of material resistance necessary for pressure casting, whereby the molding of the semi-solid becomes unstable. As a result the molding of metal products cannot be carried out. On the other hand, in a semi-solid having a solid-phase ratio higher than 75%, the thixotropy performance due to the intervening of liquid phases therein is lost and it becomes extremely difficult to pressure cast the semi-solid into a mold through a nozzle. However, when the solid phase ratio of the semi-solid is in a range of 30 to 70%, pressure casting can be easily carried out at thixotropy performance although having a difference in itself between the upper limit and the lower limit.

It is preferred that the pressure casting of the semi-solid into a mold is carried out by use of a nozzle having a diameter of 8 to 15 mm and a gate having a thickness of 1 mm or less. If this nozzle diameter and the gate thickness are used, the semi-solid is liable to receive shearing force at the time when it passes through the limited nozzle and gate. Thus the solid-phases a′ are subdivided and a metal structure having a small bias in the distribution of primary crystals a″ in a metal product can be formed.

FIGS. 6 to 9 are views of structures of metal products obtained by the steps of temperature-holding (for 25 minutes) semi-solids while providing a difference in temperature of 5° C. from 580° C. to 595° C. after setting the temperature of a heating means in a molding machine at 5° C. higher than the temperature of the semi-solids, and pressure casting each of the obtained semi-solids into a mold from a nozzle having a diameter of 8 mm through a gate having a thickness of 0.5 mm to form the metal product. In the respective structures of the semi-solids used in the molding of the metal products of FIGS. 6 to 9, the size (grain diameter) of the main solid phase is 50 μm or more although omitted in the Figures.

In the metal product molded of said semi-solid, as apparent from the view of the structure, the main primary crystal a″ is sphered in the size of 10 μm or more, and the distribution state of the crystals are uniformly dispersed in eutectic crystals b″ as a whole. The ratio of the primary crystals a″ in the metal product is increased from 46% to 50% as the temperature of the semi-solid is increased from 580° C. to 590° C. However, the primary crystal a″ of a metal product obtained from a semi-solid of 590° C. which is thought to be a liquidus line temperature is fined by melting and shearing so that the entire grain diameter of the crystal is decreased. However the size of the main primary crystal a″ is 10 um or more and the ratio of the crystal maintains 28%.

As described above, in a magnesium metal product having the primary crystal a″ ratio of 20 to 50% and the size of the main primary crystal a″ of 10 μm or more, a test piece of the product thickness of 0.8 mm can obtain effects of increases in 60 % in elongation, 20% in hardness, 30% in tensile strength and the like in comparison with a magnesium metal product molded of a molten magnesium alloy perfectly melted at a temperature of 620° C. or more, and the magnesium metal product facilitates mechanical working such as pressing, cutting and the like. Further, according to this invention, the distribution of primary crystals in a metal product are more uniform than that of a metal product obtained by a conventional thixo-molding method in which a molten material is cooled to a solid-phase and liquid-phase coexisting temperature, and is agitation sheared by screw rotation, and then the obtained material is pressure cast into a mold. Thus strength of the magnesium metal product of this invention becomes more excellent. 

1. A pressure casting method of a magnesium alloy comprising the steps of cooling a molten magnesium alloy to form a partially molten state containing a solid-phase, further cooling the partially molten state to form a solid-phase granularly crystallized solid material and partially-melting the solid material to pressure cast it into a mold by a molding machine, wherein a ratio of primary crystals of said solid material is set to 55 to 65%, the solid material is melted to be a semi-solid body having a thixotropic properties in a solid-phase and liquid-phase coexisting state so that the semi-solid having the size of a main solid phase of 50 to 250 μm and a solid-phase ratio of 30 to 70%, and pressure casting the semi-solid into a mold through a nozzle while maintaining the semi-solid state to mold metal products having a ratio of primary crystals of 20 to 50%.
 2. The pressure casting method of a magnesium alloy according to claim 1, wherein the temperature of a heating means in a molding machine for holding the semi-solid in said semi-solid state is set at a temperature 5 to 15° C. higher than the temperature of the semi-solid in accordance with time from the starting of melting of the solid material to the pressure casting of the semi-solid.
 3. The pressure casting method of a magnesium alloy according to claim 1, wherein said semi-solid is pressure cast from a nozzle having a diameter of 8 to 15 mm into a mold through a gate having a thickness of 1 mm or less.
 4. A metal product of a magnesium alloy molded by the pressure casting method of a magnesium alloy according to claim 1, comprising a metal structure whose main primary crystal is spherical and has a diameter of 10 μpm or more.
 5. The metal product of a magnesium alloy according to claim 4, wherein said metal product has a wall thickness of 0.4 to 1.5 mm, preferably 0.6 to 1.0 mm.
 6. A metal product of a magnesium alloy molded by the pressure casting method of a magnesium alloy according to claim 2, comprising a metal structure whose main primary crystal is spherical and has a diameter of 10 μm or more.
 7. A metal product of a magnesium alloy molded by the pressure casting method of a magnesium alloy according to claim 3, comprising a metal structure whose main primary crystal is spherical and has a diameter of 10 μm or more.
 8. The metal product of a magnesium alloy according to claim 6, wherein said metal product has a wall thickness of 0.4 to 1.5 mm, preferably 0.6 to 1.0 mm.
 9. The metal product of a magnesium alloy according to claim 7, wherein said metal product has a wall thickness of 0.4 to 1.5 mm, preferably 0.6 to 1.0 mm. 